Tubular ceramic-carbonate dual-phase membranes and methods of manufacture thereof

ABSTRACT

Embodiments for a tubular ceramic-carbonate dual-phase membrane and methods for manufacturing the tubular ceramic-carbonate dual-phase membrane are disclosed.

CROSS REFERENCE TO RELATED APPLICATIONS

This application claims benefit to U.S. provisional patent application Ser. No. 61/874,226, filed on Sep. 5, 2013, which is incorporated by reference in its entirety.

STATEMENT OF GOVERNMENT SPONSORED SUPPORT

This invention was made with government support under DE-FE0000470 awarded by the Department of Energy. The government has certain rights in the invention.

FIELD

This document relates to dual-phase membranes and in particular to asymmetric tubular dual-phase ceramic-carbonate membranes used for high temperature carbon dioxide separation.

BACKGROUND

Increasing carbon dioxide concentration in the atmosphere is directly related to the present environmental problems such as global warming. Power plants that burn fossil fuel generate about 40% of the CO₂ emissions worldwide. It is predicted that under a business-as-usual scenario (e.g., no CO2 emission mitigation), global CO2 emissions from coal combustion will increase from 9 Gton/year in 2000 to 32 Gton/year in 2050. Therefore, the control of CO2 emissions demands the development of new and better technologies. There different strategies are normally used to achieve CO2 separation and capture from a fossil-fired power production: post-combustion, pre-combustion and oxyfuel.

Membrane systems have the potential to separate carbon dioxide at lower costs and with lower energy penalties than other related technologies. High temperature CO₂-permselective membranes could be applied to pre and post-combustion process for CO₂ capture. Furthermore, high temperature CO₂-permselective membranes could be used in reactions involving CO₂, such as water gas shift reaction or provide other types of innovative process designs, such as integrated gasified combined cycle (IGCC). Similarly, many processes in chemical and refinery industries involve CO₂ either as a reactant or product. One reaction is dry-reforming of methane with CO₂ to produce hydrogen. High temperature CO₂-permselective membranes can be used in membrane reactors to improve the efficiency of these chemical reaction processes.

Many early efforts have been reported on developments of microporous inorganic membranes for CO₂ separation. These membranes are perm-selective for CO₂ at low temperatures only. Dense, nonporous ceramic membranes are known for the infinitely large selectivity for O₂ over N₂ and other gases, and high O₂ permeance at temperatures above 700° C. Research efforts on synthesis of dense Li₂ZrO₃ and Li₄SiO₄ membranes for high temperature separation of CO₂ were reported, but these membranes exhibit a CO₂/N₂ selectivity of about 5 and CO₂ permeance of 10⁻⁸ mol/s·Pa·m² at 525° C. It is known that molten carbonate, such as Li₂CO₃/K₂CO₃, can conduct CO₃ ²⁻ at a very high rate at high temperatures. A metal-carbonate dual-phase membrane was prepared and shown to be able to separate CO2 from N2, CO2 and O2 mixture. However, the permeation of CO₂ through the metal-carbonate membrane requires the presence of oxygen and the membrane suffers from a stability issue due to metal oxidation and metal-carbonate interaction. These problems have been addressed by replacing the metal phase with a mixed electronic-ionic conducting metal oxide phase.

Recently, the inventors have reported that a dual-phase membrane consisting of a molten carbonate (LiCO₂/Na₂CO₃/K2CO₃) entrapped in a porous perovskite-type La—Sr—Co—FeO₃ ceramic support is perm-selective to CO₂ (with CO₂/N₂ selectivity well above 225) with CO₂ permeance of above 1.0×10⁻⁸ mol/m₂·s·Pa at temperatures above 500° C. These dual-phase membranes had a thickness larger than 300 μm to 3 mm and were prepared with a disc-like configuration. However, these dual-phase membranes in a disc-like configuration having larger thicknesses were found not to have any practical applications.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is an illustration showing the various structural and operational aspects of a tubular ceramic-carbonate dual-phase membrane;

FIG. 2 is an illustration showing a sequence for manufacturing the tubular ceramic-carbonate dual-phase membrane;

FIG. 3 is a picture illustrating an embodiment of the tubular ceramic-carbonate dual phase membrane using porous Bi_(1.5)Y_(0.3)Sm_(0.2)O_(3-δ) (“BYS”), SDC or SDC/BYS tubular supports prepared using a centrifugal casting process;

FIG. 4A shows a picture of a cross-sectional view of a dual-phase membrane containing a thin dual-phase SDC-carbonate layer. FIG. 4B shows a picture of a cross-sectional view of a dual-phase membrane containing a thin dual-phase SDC-carbonate layer;

FIG. 5 is a graph showing CO₂ permeation and permeance of a SDC tubular ceramic-carbonate dual-phase membrane as a function of temperature;

FIG. 6 is a graph comparing CO₂ permeation permeance of a thick SDC-carbonate tubular ceramic-carbonate dual-phase membrane with an asymmetric, thin tubular dual-phase membrane;

FIG. 7 is a schematic showing applications of tubular ceramic-carbonate dual-phase membranes in membrane reactors for reactions with carbon dioxide removal;

FIG. 8 is a simplified block diagram illustrating a process for IGCC with CO₂ capture using a combination of the tubular ceramic-carbonate dual-phase membrane and reduced physical absorption separations;

FIG. 9 is a simplified block diagram illustrating a process for methanol production with CO₂ capture by the tubular ceramic-carbonate dual-phase membrane;

FIG. 10 is a graph showing various XRD patterns that demonstrate that SDC and BYs are chemically compatible with carbonate;

FIG. 11 is a graph showing CO₂ permeation flux and permeance of asymmetric and symmetric tubular dual-phase membranes as a function of temperature; and

FIG. 12 is a graph showing CO₂ permeation flux and permeance of asymmetric tubular dual-phase membrane as a function of feed CO₂ concentration at 900° C.

Corresponding reference characters indicate corresponding elements among the view of the drawings. The headings used in the figures should not be interpreted to limit the scope of the claims.

DETAILED DESCRIPTION

Embodiments for tubular ceramic-carbonate dual-phase membranes and method for manufacturing such dual-phase membranes are described herein. Referring to the drawings, one embodiment of a tubular ceramic-carbonate dual-phase membrane is illustrated and generally indicated as 100 in FIGS. 1-12.

As shown in FIG. 1, the tubular ceramic-carbonate dual-phase membrane 100 may be made of a porous ceramic phase that serves as an oxygen ion conductor and a carbonate phase that allows CO₂ permeation through an electrochemical conversion of carbonate ions (CO₃ ²⁻) and the subsequent transport of this ionic species across a tubular-shaped body 101 that defines the tubular ceramic-carbonate dual-phase membrane 100.

As further shown, the tubular-shaped body 101 forms an elongated channel 106 extending between a proximal opening 108 at one end and a distal opening 110 at the opposite end that forms a conduit configured to allow the passage of gas or fluid through the channel 106. In addition, the tubular-shaped body 101 includes an outer support layer 102 made from a material that is non-wettable with molten carbonate and a thin inner layer 104 made from a material that is wettable with molten carbonate. As used herein, the term “wettable” refers to the ability of a liquid to maintain contact with a solid surface which results from intermolecular interactions when the two are brought together, while the term “non-wettable” conversely refers to the inability of a liquid to maintain contact with a solid surface when the liquid and solid surface are brought together. As such, the outer support layer 102 may be made from a material that does not permit the infiltration of carbonate, while the thin inner layer 104 may be made from a material that allows the molten carbonate to infiltrate.

In some embodiments, the thin inner layer 104 may be made of an oxygen ionic or mixed ionic-electronic conducting porous ceramic material that is wettable with metal carbonate so that the pores fill with molten carbonate during the manufacturing process. The thin inner layer 104 is made from the porous ceramic material filled with carbonate that allows ionic oxygen to be conducted through the thin inner layer 104 during a CO₂ separation process.

In some embodiments, the thin inner layer 104 may have porosity in the range of 0.20 to 0.80 and a pore size that ranges from 5 nm to 5 μm. In some embodiments, the thin inner layer 104 may have a thickness that ranges substantially from 1 to 150 μm. In some embodiments, the outer support layer 102 may have porosity in the range of 0.25 to 0.75 and a pore size that ranges from 0.05 μm to 10 μm. Moreover, in some embodiments the outer support layer 102 may have a thickness that ranges substantially from 1-3 mm.

In one application, the tubular ceramic-carbonate dual-phase membrane 100 may be utilized in a CO₂ separation system that separates CO₂ under high temperature conditions. For example, in one CO₂ separation application, a CO₂-containing gas flows under high pressure through the channel 106 of the tubular ceramic-carbonate dual-phase membrane 100, while a sweep gas under lower pressure flows outside the tubular-shaped body 101 to collect CO₂ that is conducted through the thin inner layer 104 and then transported through the outer support layer 102. To achieve CO₂ permeation, the thin inner layer 104 acts as an oxygen ionic conductor for transporting CO₂ from the CO₂-containing gas flowing through the channel 106 to the sweep gas flowing outside the tubular-shaped body 101 of the tubular ceramic-carbonate dual-phase membrane 100. This permeation of CO2 through the tubular-shaped body 101 is accomplished by attaching an oxygen ion to CO₂ from the CO₂-containing gas such that the resulting CO₃ ²⁻ is conducted through the tubular-shaped body 101 where the oxygen ion detaches to allow CO₂ removed from the CO₂-containing gas to be entrained in the sweep gas. It has been found that the tubular ceramic-carbonate dual-phase membrane 100 exhibits high CO2 permeance of 1-50×10⁻⁸ mol m⁻² s⁻¹ Pa⁻¹ in a high temperature range between 500-900° C.

Referring to FIG. 2, one method for fabricating the tubular ceramic-carbonate dual-phase membrane 100 may include a centrifugal casting method. In one method, the outer support layer 102 is formed by pouring a predetermined amount a liquid suspension containing samaria doped ceria (“SDC”) and Bi_(1.5)Y_(0.3)Sm_(0.2)O_(3-δ) or bismuth-yttria-smaria (“BYS”) particles into a stainless steel tube in which the SDC/BYS suspension is non-wettable with metal carbonate and exhibits high oxygen ionic conductivity. In some embodiments, the SDC/BYS suspension may have a composition of 55 wt% SDC and 45 BYS prepared by a milling process. The SDC/BYS suspension is then spun in a centrifuge betweem 3000-5000 rpm where centrifugal force causes the outer support layer 102 made from the SDC/BYS suspension to be formed. The liquid in the middle of the stainless steel tube is then poured out. An SDC suspension in the form of an extremely diluted SDC slurry is then poured in the channel 106 defined by the outer support layer 102 and the SDC suspension is then spun in a centrifuge until the thin inner layer 104 made of SDC suspension is formed and bonds to the inner surface of the outer support layer 102 made of the SDC/BYS mixture. The thin outer support layer 102 and the thin inner layer 104 collectively form a tubular-shaped dry compact. In some embodiments, the SDC used in the outer support layer 102 and the SDC used in the thin inner layer 104 may have a different particular size and porosity. In addition, the tubular-shaped dry compact is removed from the stainless steel tube and sintered at 1150° C. for 12 hours. The tubular-shaped dry compact is then immersed in a molten carbonate that is heated to a melting temperature such that the molten carbonate contacts and fills the pores of the thin inner layer 104. In some embodiments, the molten carbonate may be poured through the channel 106 of the tubular shaped dry compact such that the molten carbonate similarly contacts and fills the pores of the thin inner layer 104. The molten carbonate bonds with the thin inner layer 104 made from a material that is wettable with carbonate, while the molten carbonate will not bond with the outer support layer 102 since the outer support layer 102 is made from a material that is non-wettable with carbonate. Due to the fact that the outer support layer 102 is made from SDC-BYS that forms a porous structure and is non-wettable with carbonate, the porous structure of this outer support layer 102 may be maintained after infiltration.

Referring to FIG. 3, a picture is shown that illustrates the porous BYS, SDC or SDC/BYS tubular-shaped bodies 101 prepared using the above centrifugal casting method.

Referring to FIG. 4A and FIG. 4B, cross-sectional views of the tubular ceramic-carbonate dual-phase membrane 100 are shown that illustrates the relative thinness 150 pm of the thin inner layer 104 made from SDC in comparison to the greater thickness of the outer support layer 102 made from SDC/BYS. FIG. 4A shows the relatively thick outer support layer 102 and the relatively thin inner layer 104, while FIG. 4B shows the cross-section of the tubular ceramic-carbonate dual-phase membranes 100 with the thin porous SDC layer filled with carbonate. In addition, the tubular ceramic-carbonate dual-phase membranes 100 are hermetic to helium as well as nitrogen or any gas other than CO₂.

Referring to FIG. 5, a graph shows CO₂ flux and permeance of the tubular ceramic-carbonate dual-phase membrane 100 using SDC as a function of temperature. In the graph, the feed side includes syngas at a flow rate of 100 ml*min⁻¹ and the sweep side includes He at a flow rate of 100 ml*min⁻¹. The tubular-shaped body 101 has a thickness of 120 μm. The tubular ceramic-carbonate dual-phase membranes 100 were studied for CO₂ separation under syngas containing CO₂, CO, N₂ and H₂ in which the tubular ceramic-carbonate dual-phase membranes 100 are perm-selective to CO₂ only. It was found that a thin membrane exhibits very high separation performance. For example, at 900° C., the CO₂ permeation flux of the tubular ceramic-carbonate dual-phase membrane 100 reached 1.63 ml*cm⁻²*min1- and 3.82×10⁻⁷ mol*s-1*Pa⁻¹, respectively, while at 700° C., the CO₂ permeation flux of the tubular ceramic-carbonate dual-phase membrane 100 reached 0.49 ml*cm⁻²*min⁻¹ and 1.05×10⁻⁷ mol*m⁻²*s⁻¹*Pa⁻¹, respectively. As such, it can be concluded that reducing the thickness of the tubular-shaped body 101 improves CO₂ permeation performance.

In addition, the stability of the tubular ceramic-carbonate dual-phase membrane 100 was investigated under a syngas atmosphere. Referring to FIG. 6, a graph shows the comparison of CO₂ permeation permeance of a thick (2 mm) SDC-carbonate tubular and asymmetric, thin (150 μm) tubular dual-phase membrane 100 with synthetic syngas as the feed gas and He as the sweep gas with both gases at 100 ml*min⁻¹, at a pressure of 1 atmosphere. As shown, the CO₂ permeances of the tubular ceramic-carbonate dual-phase membranes 100 were stable during the operating period. The results confirm that the tubular ceramic-carbonate dual-phase membranes 100 have a potential for practical application in pre-combustion CO₂ capture.

There are major applications for tubular ceramic-carbonate dual-phase membranes 100 in membrane reactors for reactions involving carbon dioxide as a reactant or by-product. These reactions are found in many chemical and energy production processes. For example there are two representative processes. First, a water gas shift (WGS) reaction:

CO+H₂0>>CO₂+H₂

The other is a steam reforming reaction or gasification reaction:

CH_(x)+H₂0>>CO₂+CO+H₂

Both reactions operate at high temperatures and high pressure. Such high pressure provides a driving force for CO2 to permeate through the membrane wall, thereby resulting in enhanced conversion and production of hydrogen at high pressure as shown in FIG. 7, which shows a schematic of the various applications for tubular ceramic-carbonate dual-phase membranes 100 in membrane reactors with carbon dioxide removal.

Referring to FIG. 8, a simplified block diagram shows the process flow for an Integrated Gasification Combined Cycle (“IGCC”) with CO₂ capture using a combination of the tubular ceramic-carbonate dual-phase membrane 100 to remove 90% of the CO₂ in the raw syngas prior to the water gas shift reaction (WGS). There are four potential advantages to using this process: (1) the high pressure of the raw syngas provides high driving force for CO₂ separation by the tubular ceramic-carbonate dual-phase membrane 100, which allows for the capture of 90% of CO₂ from raw syngas using a relatively small membrane area due to the tubular configuration of the tubular ceramic-carbonate dual-phase membrane 100; (2) the raw syngas is at temperatures over 800° C., which is ideal temperature range for use of the tubular ceramic-carbonate dual-phase membrane 100 to achieve high CO₂ permeance; (3) reduced CO₂ levels in the raw syngas before the downstream WGS reactor facilitate the conversion of CO₂ into H₂, and therefore improves the process efficiency of the WGS step, especially in the case of WGS membrane reactor; and (4) Because a portion of the CO₂ is removed from the raw syngas by the dual-phase membranes before the downstream WGS reaction, less CO₂ needs to be captures after the WGS step.

Referring to FIG. 9, a simplified block diagram shows the process flow for methanol production with CO₂ capture using the tubular ceramic-carbonate dual-phase membrane 100. For coal to methanol conversion, the tubular ceramic-carbonate dual-phase membrane 100 can be used for CO₂ capture from gasification gas prior to the WGS step shown in FIG. 9. The process that uses the tubular ceramic-carbonate dual-phase membrane 100 can take advantage of the high pressure of raw syngas for providing a large driving force, which partially reduces the load of the downstream physical absorption separation of CO₂, thus reducing significantly the energy cost for CO₂ capture. In addition, the lowering CO₂ content in the treated raw syngas can facilitate the WGS reaction. The size of the WGS reactor can also be reduced due to the smaller volume of the raw syngas steam after CO₂ removal. Further, the upstream CO₂ capture may assist in increasing H₂/CO or H₂/CO₂ ratios required for methanol synthesis.

Additional details of the tubular ceramic-carbonate dual-phase membrane 100 may be found in the inventors' publication entitled “Asymmetric Tubular Ceramic-Carbonate Dual Phase Membrane for High Temperature CO₂ Separation”, which provides a description of a tubular ceramic-carbonate dual-phase membrane and a comparison with a ceramic-carbonate dual-phase membrane having a disc-like configuration. The above publication is incorporated by reference in its entirety and attached hereto as Addendum A.

Additional details for manufacturing the tubular ceramic-carbonate dual-phase membrane 100 may be found in a second publication entitled “Centrifugal Slip Casting of Asymmetric Tubular Ionic Conducting Ceramic-Carbonate Dual-Phase Membranes for CO₂ Separation” provides a description of a centrifugal slip casting process for manufacturing the tubular ceramic-carbonate dual-phase membrane 100. The above publication is incorporated by reference in its entirety and is attached hereto as Addendum B.

Moreover, additional experimental details related to the tubular ceramic-carbonate dual-phase membrane 100 conducted by the inventors are disclosed under a paper entitled “Supporting Information—Asymmetric Tubular Ceramic-Carbonate Dual-Phase Membrane for High Temperature CO₂ Separation”, which is incorporated by reference in its entirety and attached hereto as Addendum C.

Finally, a PowerPoint presentation directed to aspects of the tubular ceramic-carbonate dual-phase membrane 100 entitled “Pre-Combustion Carbon Dioxide Capture by a New Dual-Phase Ceramic-Carbonate Membrane Reactor” is also incorporated by reference in its entirety and attached hereto as Addendum D.

TESTING

The crystal structures of porous SDC-BYS support of the outer support layer 102 and the SDC-carbonate of the thin inner layer 104 for the tubular ceramic-carbonate dual-phase membrane 100 were analyzed first to confirm the chemical compatibility of SDC, BYS and carbonate. As shown in 10(a) and 10(b), the SDC and BYS exhibit typical fluorite structure. From FIG. 10( c), the SDC and BYS phase are observed in the porous support, indicating that SDC is chemical compatible with BYS. FIG. 10( c) exhibits mixed crystal phases of SDC and carbonate. Two carbonate diffraction peaks can be found from 20 to 25 degrees. No obvious impurity phase can be observed, thereby suggesting that SDC and BYS are chemically compatible with carbonate.

For the tubular ceramic-carbonate dual-phase membrane 100, the microstructure (pore size and porosity) of the porous ceramic substrate is closely related to the CO₂ separation performance. As shown in FIG. 2 of the publication attached as Addendum A, the thin inner layer 104 made from SDC with a thickness of about 150 μm is well bound with the outer support layer 104 made from SDC-BYS. The thin inner layer 104 had a high porosity and uniform pore structure (FIG. 2B of Addendum A). The average porotsity of the SDC/SDC-BYS substrate was estimated to be 35%±5%. At high temperature, the porous SDC of the thin inner layer 104 was infiltrated with molten carbonate. After infiltration, the thin inner layer 104 is dense, whereas the outer support layer 102 made from SDC-BYS is still porous because of the carbonate non-wettable property of BYS (FIG. 2C of Addendum A). From FIG. 2D of Addendum A, SDC and carbonate phases can be distinguished easily and are well mixed. The off-white phase with clear grain boundary is SDC, while the dark grey phase is carbonate.

The asymmetric tubular SDC-carbonate dual phase membrane with the separation layer of 150 μm and the porous support of about 1.5 mm was applied to evaluate the CO₂ permeation performance. For comparison, the CO₂ permeation through the symmetric tubular SDC-carbonate membrane with the thickness of 1.5 mm was tested as well. The temperature dependence of CO₂ permeation flux and CO2 permeance of the asymmetric and symmetric membranes are shown in FIG. 11. Both CO₂ flux and permeance increase with increasing temperature. At 900° C., the CO₂ flux and permeance of the asymmetric membrane are 1.56 ml·cm⁻²·min⁻¹ and 2.33×10^(−7 mol·m) ⁻²·s⁻¹·Pa⁻¹, respectively, which are 3 times that of the symmetric membrane. At 800° C., the difference reaches 3.6 times. Therefore, reducing the thickness of the membrane is an effective route to improve the CO₂ permeation performance. Because of the gas transport resistance of the porous SDC-BYS support, however, the increase of CO₂ flux and permeance is not as large as the reducing of membrane thickness (nearly 10 times). This was also observed in preparing asymmetric mixed-conducting membranes.

The CO₂ permeation activation energy of the asymmetric membrane is about 60.3 kJ·mol⁻¹ (FIG. 11), which is lower than that of the symmetric tubular membrane (81.2 kJ·mol⁻¹) but close to that of the reported disk thick membrane with similar SDC and carbonate composition. The difference of the activation energy is caused by the different microstructure of the SDC substrate. The asymmetric SDC/SDC-BYS substrate sintered at relatively lower temperature (1120° C.) than the symmetric SDC substrate (1420° C.), therefore the porosity may be relatively high, leading to high ratio of carbonate to SDC in the membrane. Generally, the high relative amount of carbonate in the membrane results in low CO₂ permeation activation energy because the activation energy of carbonate ionic conductivity of the carbonate phase is lower than oxygen ionic conductivity of the SDC phase. Similar result was reported by Boden et al. It was observed that the ionic conductivities activation energies of SDC and (Li/Na)₂CO₃ composite electrolytes decreased with increasing the relative amount of carbonate phase.

CO₂ concentration in the feed side is also an important factor that affects the CO₂ permeation. As shown in FIG. 12, At 700° C. the CO₂ flux increases from 0.17 to 0.50 ml·cm⁻²·min⁻¹ with increasing the feed CO₂ concentration from 10% to 90%, while the permeance decreases from 1.27×10⁻⁷ to 0.41×10⁻⁷ mol·m⁻²·s⁻¹·Pa⁻¹. This result can be explained by the CO₂ permeation modeling. According to the modeling, CO₂ flux and permeance for the SDC-carbonate dual-phase membranes can be expressed as

I_(CO) ₂ ∞[P′_(CO) ₂ ^(n)−P″_(CO) ₂ ^(n)]  (1)

and

F_(CO) ₂ ∞[P′_(CO) ₂ ^(n)−P″_(CO) ₂ ^(n)]/[P′_(CO2)−P″_(CO2)]  (2)

wherein J_(CO2) and F_(CO2) are the CO₂ flux and permeance, respectively. The P′_(CO2) is the CO₂ partial pressure in the feed side. As the CO₂ partial pressure increases from 0.1 to 0.9 atm, CO₂ flux is an increasing function, whereas CO₂ permeance is a decreasing function. For typical flue gas from coal-fired power plant, CO₂ concentration is 15-16%. For this feed CO₂ concentration, the CO₂ permeance is estimated to be 1.16×10⁻⁷ mol·m⁻²·s⁻¹·Pa⁻¹ at 700° C. Therefore, the dense dual-phase membrane is really promising for CO₂ capture from high temperature flue gas.

It should be understood from the foregoing that, while particular embodiments have been illustrated and described, various modifications can be made thereto without departing from the spirit and scope of the invention as will be apparent to those skilled in the art. Such changes and modifications are within the scope and teachings of this invention as defined in the claims appended hereto. 

What is claimed is:
 1. A tubular dual-phase membrane comprising: a tubular-shaped body comprising: an outer support layer comprising a first ceramic material that is non-wettable with carbonate; a thin inner layer bonded to the outer support layer made from a second ceramic material that is wettable with carbonate; and a channel defined by the thin inner layer, wherein the channel is in communication with a proximal opening at a first end of the tubular body and a distal opening at a second end of the tubular body.
 2. The tubular dual-phase membrane of claim 1, wherein the first ceramic material comprises a solid oxide electrolyte.
 3. The tubular dual-phase membrane of claim 2, wherein the solid oxide electrolyte comprises at least one of yttria doped zirconia (YSZ), gadolinia doped ceria (CGO), and samaria doped ceria (SDC).
 4. The tubular dual-phase membrane of claim 1, wherein second ceramic material comprises at least one of a sameria doped ceria and a bismuth-yttria-smaria (“BYS”).
 5. The tubular dual-phase membrane of claim 1, wherein the first ceramic material is bonded to carbonate.
 6. The tubular dual-phase membrane of claim 1, wherein the outer support layer has a thickness in a range of between 1 mm to 3 mm.
 7. The tubular dual-phase membrane of claim 1, wherein the thin inner layer has a thickness in a range of between 1 to 150 μm.
 8. A tubular dual-phase membrane comprising: a tubular-shaped body comprising: a solid porous ceramic phase made from a material that is non-wettable with carbonate and serves as an oxygen ion conductor; a molten carbonate phase made from a material that comprises carbonate; and a channel defined by the molten carbonate phase, wherein the channel is in communication with a proximal opening at a first end of the tubular-shaped body and a distal opening at a second end of the tubular-shaped body
 9. The tubular dual-phase membrane of claim 8, wherein the molten carbonate phase is wettable with carbonate.
 10. The tubular dual-phase membrane of claim 8, wherein the solid porous ceramic phase forms an outer support layer and the molten carbonate phase forms an inner layer of the tubular-shaped body.
 11. A method for manufacturing a tubular dual-phase membrane comprising: spinning a first suspension in a centrifuge, wherein the first suspension comprises bismuth-yttria-smaria (“BYS”) poured into a container, wherein the BYS forms an outer layer after being spun in the centrifuge; spinning a second suspension in a centrifuge, wherein the second suspension comprises samaria doped ceria (“SDC”), wherein the SDC forms an inner layer that bonds with the outer layer to form a substantially tubular-shaped body after being spun in the centrifuge; removing the substantially tubular-shaped body from the container; and immersing the substantially tubular-shaped body in molten carbonate, wherein the molten carbonate is wettable with the inner layer and non-wettable with the second layer such that the molten carbonate bonds with the inner layer.
 12. The method of claim 11, further comprising: sintering the substantially tubular-shaped body after the substantially tubular-shaped body is immersed in molten carbonate.
 13. The method of claim 11, further comprising: removing a liquid solvent after the step of spinning the first suspension in the centrifuge.
 14. The method of claim 11, wherein the first suspension and the second suspension are spun in the centrifuge at substantially 4,000 rpm.
 15. The method of claim 11, wherein the outer layer defines a channel after the first suspension is spun in the centrifuge. 